US4624705A - Mechanical alloying - Google Patents

Mechanical alloying Download PDF

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Publication number
US4624705A
US4624705A US06/848,162 US84816286A US4624705A US 4624705 A US4624705 A US 4624705A US 84816286 A US84816286 A US 84816286A US 4624705 A US4624705 A US 4624705A
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US
United States
Prior art keywords
aluminum
alloy
mechanical alloying
base alloy
titanium
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Expired - Fee Related
Application number
US06/848,162
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English (en)
Inventor
Arun D. Jatkar
Paul S. Gilman
Raymond C. Benn
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Huntington Alloys Corp
Original Assignee
Inco Alloys International Inc
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Priority to US06/848,162 priority Critical patent/US4624705A/en
Application filed by Inco Alloys International Inc filed Critical Inco Alloys International Inc
Assigned to INCO ALLOYS INTERNATIONAL, INC. reassignment INCO ALLOYS INTERNATIONAL, INC. ASSIGNMENT OF ASSIGNORS INTEREST. Assignors: BENN, RAYMOND C., GILMAN, PAUL S., JATKAR, ARUN D.
Publication of US4624705A publication Critical patent/US4624705A/en
Application granted granted Critical
Priority to AU70938/87A priority patent/AU588990B2/en
Priority to BR8701509A priority patent/BR8701509A/pt
Priority to DE8787302943T priority patent/DE3774169D1/de
Priority to EP87302943A priority patent/EP0244949B1/en
Priority to ES198787302943T priority patent/ES2025651T3/es
Priority to AT87302943T priority patent/ATE69065T1/de
Priority to JP62082789A priority patent/JPS62238344A/ja
Assigned to HUNTINGTON ALLOYS CORPORATION reassignment HUNTINGTON ALLOYS CORPORATION RELEASE OF SECURITY INTEREST Assignors: CREDIT LYONNAIS, NEW YORK BRANCH, AS AGENT
Anticipated expiration legal-status Critical
Expired - Fee Related legal-status Critical Current

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Classifications

    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C32/00—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ
    • C22C32/0047—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents
    • C22C32/0052—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents only carbides
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/10—Alloys containing non-metals
    • C22C1/1084—Alloys containing non-metals by mechanical alloying (blending, milling)

Definitions

  • the present invention is concerned with the manufacture of aluminum-base alloys having useful characteristics at temperatures up to about 480° C. by virtue of incorporating carbides, more stable than aluminum carbide in the alloys at those temperatures.
  • High strength aluminum-base alloys i.e., alloys containing greater than 50% by weight aluminum have been made by mechanical alloying techniques which alloys have useful mechanical characteristics at room temperature. These alloys depend in part for strength on age hardened and/or work hardened internal structures and, in part, on the formation, in-situ, of a fine dispersion of aluminum carbide (Al 4 C 3 ) and aluminum oxide by reaction of aluminum with the break-down products of a carbon-containing processing aid (e.g., stearic acid) used in the mechanical alloying process.
  • a carbon-containing processing aid e.g., stearic acid
  • the present invention contemplates including in the mechanical alloying charge for an aluminum-base alloy, a material in microfine dispersion or readily transformable to a microfine dispersion which comprises or contains a carbide-forming element from the group of titanium, niobium, zirconium, vanadium, hafnium and molybdenum, along with aluminum and other alloying elements, mechanically alloying such charge in the presence of a carbon-containing processing aid to thereby mechanically alloy the charge and form, in-situ within the alloyed charge a dispersion of carbidiferous material incorporating metal of the aforementioned group, said carbidiferous material being present as dispersed particles less than about 500 A in major dimension and said dispersion being resistant to coarsening at temperatures above 200° C.
  • a material in microfine dispersion or readily transformable to a microfine dispersion which comprises or contains a carbide-forming element from the group of titanium, niobium, zirconium, vanadium, hafnium and
  • the invention also contemplates the alloys made by the aforedescribed process.
  • the carbide-forming element is present in the alloy produced in an amount at least equal to the stoichiometric amount minimally necessary to combine with carbon present in the alloy.
  • the amount of vanadium in the alloy advantageously is at least that amount calculated from the formula VC.
  • mechanical alloying is employed to mean a process in which a charge of powder ingredients is subjected to impacts by an impacting medium so as to cause a multiplicity of particle weldings and fracturing until the charge is converted to an essentially uniform powder product. While attritors and horizontal ball mills are most often used for mechanical alloying, for purposes of the invention the particular apparatus used is immaterial. The product of mechanical alloying is thereafter compressed, sintered and worked as disclosed hereinafter.
  • carbiferous material is employed to include not only simple carbides e.g., TiC, VC, V 2 C, NbC, Nb 2 C, but also compounds and mixtures such as carbonitrides, carbides containing free carbon and carbidic species formed from the association of stable carbides with one or more ingredients of alloys contemplated herein.
  • microfine dispersion means a dispersion having particle sizes significantly below 5 micrometers ( ⁇ m) average particle size and more preferably below about 1 ⁇ m in particle size.
  • Additions of strong carbide former to the mechanical alloying charge can thus be in the form of dust or fume size particles of elements or compounds or alloys of elements mentioned hereinbefore or in the form of larger size, brittle materials (e.g., intermetallic compounds) which are readily broken down by mechanical impact in the mechanical alloying process to particles less than 1 ⁇ m or, more preferably, less than 0.8 ⁇ m in average dimension.
  • Carbon-containing processing aids useful in mechanical alloying of aluminum-base alloys include stearic acid, methanol, graphite, oxalic acid, etc.
  • a powder of a brittle intermetallic compound containing the carbide-forming element is advantageous to employ in the mechanical alloying charge.
  • brittle, intermetallic compounds are VAl 3 , TiAl 3 , ZrAl 3 , NbAl 3 , FeTi, Fe 0 .85 Mn 0 .15 Ti, Ti 2 Ni, Ti 5 Si 3 , Zr 2 Si and TiFe 2 .
  • carbide-forming elements in the form of rapidly solidified particulates of alloys of the carbide-forming elements and other metals.
  • Such particulates may have the characteristics of amorphous "glassy” alloys or supersaturated solid solution alloys or may contain almost microscopically indistinguishable crystallites of a solid phase or phases normally existing at or just below the liquidus of the particular alloy system employed.
  • Powder charges in accordance with the present invention are all processed by mechanical alloying.
  • This technique can be a high energy milling process, which is described in U.S. Pat. Nos. 3,591,362, 3,740,210 and 3,816,080 (among others).
  • the aluminum-base alloy is prepared by subjecting a powder charge to dry, high energy milling in the presence of a grinding medium, e.g., balls, and a process control agent, under conditions sufficient to comminute the powder particles of the charge, and through a combination of comminution and welding actions caused repeatedly by the milling, to create new, dense, composite particles containing fragments of the initial powder material intimately associated and uniformly interdispersed.
  • Milling is done in a protective atmosphere, e.g., under an argon or nitrogen blanket, thereby facilitating oxygen control since virtually the only sources of oxygen are the starting powders and the process control agent.
  • the process control agent is a weld-controlling amount of a carbon-contributing agent.
  • the formation of dispersion strengthened mechanically alloyed aluminum is given in detail in U.S. Pat. Nos. 3,740,210 and 3,816,080, mentioned above.
  • the powder is prepared in an attritor using a ball-to-powder weight ratio of 15:1 to 60:1.
  • Preferably process control agents are methanol, stearic acid or graphite.
  • Carbon from these organic compounds and/or graphite is incorporated in the powder and contributes to the dispersoid content.
  • Carbide forming elements should be present in the charge at least in an amount approximately that stoichiometrically equivalent to about one half of the carbon entering the charge and up to about 200% or more in excess of the stoichiometric equivalent of the carbon entering the charge.
  • mechanically alloy an aluminum-rich fraction of the mill charge for a significant amount of time prior to introducing into the mill harder ingredients of the charge.
  • the alloys of the present invention produced by the process of the present invention contain oxygen in the form of stable metal oxides, e.g. Al 2 O 3 .
  • This oxygen is derived from oxide present on the powder particles introduced into the mechanical alloying apparatus, from the atmosphere present in the apparatus during mechanical alloying and, usually, from the processing aid used. While in theory it may be possible to supply metal, e.g. aluminum, powder free of oxide film and mechanically alloy such powder in an atmosphere totally devoid of oxygen, e.g. an atmosphere of argon with an oxygen-free processing aid, e.g.
  • alloys of the invention oxygen in an amount up to about 1% or even higher is not necessarily bad. Accordingly when it is desired to have oxygen contents on the high side one may very well select a processing aid such as oxalic acid which, as the monohydrate, contains about 64% oxygen.
  • a processing aid such as oxalic acid which, as the monohydrate, contains about 64% oxygen.
  • the carbon content of the alloys of the present invention is derived primarily or exclusively from the processing aid.
  • Use of 2% stearic acid as a processing aid will contribute about 1.4% carbon to a mechanically alloyed charge. However a portion of this carbon may not report in the product alloy because of the formation of carbon oxides which may escape from the milling means.
  • Degassing and compacting are effected under vacuum and generally carried out at a temperature in the range of about 480° C. (895° F.) up to just below incipient liquification of the alloy.
  • the degassing temperature should be higher than any temperature to be subsequently experienced by the alloy.
  • Degassing is preferably carried out, for example, at a temperature in the range of from about 480° C. (900° F.) up to 545° C. (1015° F.) and more preferably above 500° C. (930° F.). Pressing is carried out at a temperature in the range of about 545° C. (1015° F.) to about 480° C. (895° F.).
  • the degassing and compaction are carried out by vacuum hot pressing (VHP).
  • VHP vacuum hot pressing
  • the degassed powder may be upset under vacuum in an extrusion press.
  • compaction should be such that the porosity is isolated thereby avoiding internal contamination of the billet by the extrusion lubricant. This is achieved by carrying out compaction to at least about 95% of full density.
  • the powders are compacted to 99% of full density and higher, that is, to substantially full density.
  • Consolidation is carried out by extrusion.
  • the extrusion of the material not only is necessary to insure full density in the alloy, but also to break up surface oxide on the particles.
  • the extrusion temperature may be of significance in that control within a narrow temperature established for each alloy may optimize mechanical characteristics.
  • Lubrication practice and the exact die-type equipment used for extrusion can also be of significance to mechanical characteristics.
  • Hot compaction and hot consolidation each alone or together with heating cycles serve to totally sinter bond the product of mechanical alloying and together provide a body of substantially full density.
  • billets can be forged. If necessary, the billets may be machined to remove surface imperfections. Following forging and before or after any finishing operations the alloy can be age-hardened if it is amenable to age-hardening.
  • alloys of the invention containing carbides more thermally stable than aluminum carbide may be used in the extruded condition as well as in the forged condition. Thus heat treatment, if any, is carried out after the last appropriate working operation.
  • titanium is highly advantageous in that it has a relatively low density and its carbide has a high negative heat of formation. Vanadium is a second choice based principally on density. It is to be appreciated that when an oxygen-containing process control agent such as stearic acid is used in the mechanical alloying operation, carbon monoxide, water vapor and carbon dioxide will exist in the mill atmosphere as breakdown products of the process control agent. Under such circumstances, titanium will compete with aluminum as an oxide former and therefor the amount of titanium available to form carbides will be less than if graphite or an oxygen-poor hydrocarbon is used as process control agent.
  • an oxygen-containing process control agent such as stearic acid
  • compositions to be prepared by mechanical alloying in percent by weight as set forth in Table I.
  • the amount of processing aid is generally between 1% and 2% by weight.
  • the charges of the foregoing Table are degassed, compacted and extruded as disclosed hereinbefore to provide product which contains a refractory oxide and in which a significant amount of carbon is present as a carbide more thermally stable at temperature in the range of 100° C. to about 480° C. than aluminum carbide.
  • Precursors of the compositions of Table II are made by melting aluminum together with any one or more of chromium, molybdenum, tungsten, manganese, titanium, iron, cobalt, nickel and vanadium (i.e., elements having a low diffusion rate in solid aluminum at temperatures above about 300° C.) together with copper and silicon, if any, to form a uniform molten composition and atomizing the molten metal to form alloy powder.
  • This step is taught in any one or more of U.S. Pat. Nos. 2,966,731, 2,966,732, 2,966,733, 2,966,734, 2,966,735, 2,966,736 and 2,967,351 the disclosures of which are incorporated herein by reference.
  • the atomized powder thus formed is then subjected to mechanical alloying in the presence of a carbon-containing processing aid to include therein dispersion of a carbidiferous material more stable than aluminum carbide and, usually, a refractory oxide containing aluminum.
  • the resultant mechanically alloyed powder is then compacted, sintered and worked to the desired configuration as described hereinbefore.
  • the charges of the foregoing Table are degassed, compacted and extruded as disclosed hereinbefore to provide product in which a significant amount of carbon is present as a carbide more thermally stable at temperature in the range of 370° C. to about 480° C. than aluminum carbide.
  • Supplementing or in part substituting for stabilization of carbides is the addition of a rare earth element or elements to high temperature aluminum-base alloys.
  • a rare earth element or elements to high temperature aluminum-base alloys.
  • the metal is advantageously yttrium or lanthanum or a commercially available mixture of rare earth metals such as mischmetal, cerium-free mischmetal or lanthanum-free mischmetal.
  • Illustrative compositions in percent by weight are set forth in Table III.
US06/848,162 1986-04-04 1986-04-04 Mechanical alloying Expired - Fee Related US4624705A (en)

Priority Applications (8)

Application Number Priority Date Filing Date Title
US06/848,162 US4624705A (en) 1986-04-04 1986-04-04 Mechanical alloying
AU70938/87A AU588990B2 (en) 1986-04-04 1987-04-01 Sintered and worked aluminium-base alloys
BR8701509A BR8701509A (pt) 1986-04-04 1987-04-02 Liga com base de aluminio sinterizada e mecanicamente trabalhada;processo para producao dessa liga
JP62082789A JPS62238344A (ja) 1986-04-04 1987-04-03 機械的合金化
DE8787302943T DE3774169D1 (de) 1986-04-04 1987-04-03 Herstellung einer stabilen karbid enthaltenden aluminiumlegierung durch mechanisches legieren.
AT87302943T ATE69065T1 (de) 1986-04-04 1987-04-03 Herstellung einer stabilen karbid enthaltenden aluminiumlegierung durch mechanisches legieren.
EP87302943A EP0244949B1 (en) 1986-04-04 1987-04-03 Manufacturing of a stable carbide-containing aluminium alloy by mechanical alloying
ES198787302943T ES2025651T3 (es) 1986-04-04 1987-04-03 Produccion de una aleacion de aluminio estable que contiene carburo por aleado mecanico.

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Application Number Priority Date Filing Date Title
US06/848,162 US4624705A (en) 1986-04-04 1986-04-04 Mechanical alloying

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Country Status (8)

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US (1) US4624705A (ja)
EP (1) EP0244949B1 (ja)
JP (1) JPS62238344A (ja)
AT (1) ATE69065T1 (ja)
AU (1) AU588990B2 (ja)
BR (1) BR8701509A (ja)
DE (1) DE3774169D1 (ja)
ES (1) ES2025651T3 (ja)

Cited By (34)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4707332A (en) * 1985-02-16 1987-11-17 Mtu Moroten-Und Turbinen-Union Muenchen Gmbh Sintering process for prealloyed powders
US4729790A (en) * 1987-03-30 1988-03-08 Allied Corporation Rapidly solidified aluminum based alloys containing silicon for elevated temperature applications
US4735770A (en) * 1986-02-05 1988-04-05 Siemens Aktiengesellschaft Method for producing an amorphous material in powder form by performing a milling process
US4749545A (en) * 1986-04-02 1988-06-07 British Petroleum Co. P.L.C. Preparation of composites
US4762678A (en) * 1987-11-03 1988-08-09 Allied-Signal Inc. Method of preparing a bulk amorphous metal article
US4762677A (en) * 1987-11-03 1988-08-09 Allied-Signal Inc. Method of preparing a bulk amorphous metal article
US4787943A (en) * 1987-04-30 1988-11-29 The United States Of America As Represented By The Secretary Of The Air Force Dispersion strengthened aluminum-base alloy
US4818481A (en) * 1987-03-09 1989-04-04 Exxon Research And Engineering Company Method of extruding aluminum-base oxide dispersion strengthened
US4832734A (en) * 1988-05-06 1989-05-23 Inco Alloys International, Inc. Hot working aluminum-base alloys
US4834810A (en) * 1988-05-06 1989-05-30 Inco Alloys International, Inc. High modulus A1 alloys
US4859413A (en) * 1987-12-04 1989-08-22 The Standard Oil Company Compositionally graded amorphous metal alloys and process for the synthesis of same
US4917858A (en) * 1989-08-01 1990-04-17 The United States Of America As Represented By The Secretary Of The Air Force Method for producing titanium aluminide foil
US4923532A (en) * 1988-09-12 1990-05-08 Allied-Signal Inc. Heat treatment for aluminum-lithium based metal matrix composites
US4933007A (en) * 1988-10-21 1990-06-12 Showa Aluminum Heat-resistant aluminum-base composites and process of making same
US4946500A (en) * 1988-01-11 1990-08-07 Allied-Signal Inc. Aluminum based metal matrix composites
US4977036A (en) * 1979-03-30 1990-12-11 Alloy Surfaces Company, Inc. Coating and compositions
EP0427492A1 (en) * 1989-11-06 1991-05-15 Inco Alloys International, Inc. Aluminum-base composite alloy
WO1991007243A1 (en) * 1989-11-09 1991-05-30 Allied-Signal Inc. Dual processing of aluminum base metal matrix composites
US5028301A (en) * 1989-01-09 1991-07-02 Townsend Douglas W Supersaturation plating of aluminum wettable cathode coatings during aluminum smelting in drained cathode cells
US5039476A (en) * 1989-07-28 1991-08-13 Ube Industries, Ltd. Method for production of powder metallurgy alloy
US5100869A (en) * 1988-03-14 1992-03-31 Tsuyoshi Masumoto Process for producing metal oxide-type superconductive material
EP0487276A1 (en) * 1990-11-19 1992-05-27 Inco Alloys International, Inc. High temperature aluminum-base alloy
EP0501691A1 (en) * 1991-02-28 1992-09-02 Inco Alloys International, Inc. Intermediate temperature aluminium base alloy
US5147449A (en) * 1988-04-20 1992-09-15 Fried. Krupp Gesellschaft Mit Beschrankter Haftung Process for production of metal-metalmetalloid powders with their articles having ultramicrocrystalline to nanocrystalline structure
USRE34262E (en) * 1988-05-06 1993-05-25 Inco Alloys International, Inc. High modulus Al alloys
US5227045A (en) * 1989-01-09 1993-07-13 Townsend Douglas W Supersaturation coating of cathode substrate
US5338330A (en) * 1987-05-22 1994-08-16 Exxon Research & Engineering Company Multiphase composite particle containing a distribution of nonmetallic compound particles
US5368812A (en) * 1990-06-12 1994-11-29 Australian National University Metal carbides and derived composites made by milling to obtain a particular nanostructural composite powder
USH1411H (en) * 1992-11-12 1995-02-07 Deshmukh; Uday V. Magnesium-lithium alloys having improved characteristics
US20030056928A1 (en) * 2000-03-13 2003-03-27 Takashi Kubota Method for producing composite material and composite material produced thereby
CN100376705C (zh) * 2002-12-11 2008-03-26 山东大学 氧化铝-碳化钛粒子增强铝基复合材料的制备方法
US20110189497A1 (en) * 2008-08-08 2011-08-04 Nihon University Pure-aluminum structural material with high specific strength consolidated by giant-strain processing method
US9945018B2 (en) 2014-11-26 2018-04-17 Honeywell International Inc. Aluminum iron based alloys and methods of producing the same
US20210029969A1 (en) * 2018-02-07 2021-02-04 Idexx Laboratories, Inc. Animal Cage-Sample Collection Apparatus

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Publication number Priority date Publication date Assignee Title
AU7162191A (en) * 1989-11-09 1991-06-13 Allied-Signal Inc. Dual processing of aluminum base alloys
JP2726818B2 (ja) * 1991-04-26 1998-03-11 工業技術院長 機械的合金化法を用いた微細炭化物分散合金の作製法
WO1999027146A1 (en) * 1997-11-20 1999-06-03 Tübitak-Marmara Research Center In situ process for producing an aluminium alloy containing titanium carbide particles

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US4532106A (en) * 1980-07-31 1985-07-30 Inco Alloys International, Inc. Mechanically alloyed dispersion strengthened aluminum-lithium alloy
US4557893A (en) * 1983-06-24 1985-12-10 Inco Selective Surfaces, Inc. Process for producing composite material by milling the metal to 50% saturation hardness then co-milling with the hard phase

Cited By (41)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4977036A (en) * 1979-03-30 1990-12-11 Alloy Surfaces Company, Inc. Coating and compositions
US4707332A (en) * 1985-02-16 1987-11-17 Mtu Moroten-Und Turbinen-Union Muenchen Gmbh Sintering process for prealloyed powders
US4735770A (en) * 1986-02-05 1988-04-05 Siemens Aktiengesellschaft Method for producing an amorphous material in powder form by performing a milling process
US4749545A (en) * 1986-04-02 1988-06-07 British Petroleum Co. P.L.C. Preparation of composites
US4818481A (en) * 1987-03-09 1989-04-04 Exxon Research And Engineering Company Method of extruding aluminum-base oxide dispersion strengthened
US4729790A (en) * 1987-03-30 1988-03-08 Allied Corporation Rapidly solidified aluminum based alloys containing silicon for elevated temperature applications
US4787943A (en) * 1987-04-30 1988-11-29 The United States Of America As Represented By The Secretary Of The Air Force Dispersion strengthened aluminum-base alloy
US5338330A (en) * 1987-05-22 1994-08-16 Exxon Research & Engineering Company Multiphase composite particle containing a distribution of nonmetallic compound particles
WO1989004225A1 (en) * 1987-11-03 1989-05-18 Allied-Signal Inc. A method of preparing a bulk amorphous metal article
WO1989004226A1 (en) * 1987-11-03 1989-05-18 Allied-Signal Inc. A method of preparing a bulk amorphous metal article
US4762677A (en) * 1987-11-03 1988-08-09 Allied-Signal Inc. Method of preparing a bulk amorphous metal article
US4762678A (en) * 1987-11-03 1988-08-09 Allied-Signal Inc. Method of preparing a bulk amorphous metal article
US4859413A (en) * 1987-12-04 1989-08-22 The Standard Oil Company Compositionally graded amorphous metal alloys and process for the synthesis of same
US4946500A (en) * 1988-01-11 1990-08-07 Allied-Signal Inc. Aluminum based metal matrix composites
US5100869A (en) * 1988-03-14 1992-03-31 Tsuyoshi Masumoto Process for producing metal oxide-type superconductive material
US5147449A (en) * 1988-04-20 1992-09-15 Fried. Krupp Gesellschaft Mit Beschrankter Haftung Process for production of metal-metalmetalloid powders with their articles having ultramicrocrystalline to nanocrystalline structure
EP0339366B1 (de) * 1988-04-20 1993-08-18 Fried. Krupp AG Hoesch-Krupp Verfahren zur Herstellung von Metall-Metallmetalloid-Pulver, dessen Pulverteilchen feinstkristalline bis nanokristalline Struktur haben
US4832734A (en) * 1988-05-06 1989-05-23 Inco Alloys International, Inc. Hot working aluminum-base alloys
USRE34262E (en) * 1988-05-06 1993-05-25 Inco Alloys International, Inc. High modulus Al alloys
US4834810A (en) * 1988-05-06 1989-05-30 Inco Alloys International, Inc. High modulus A1 alloys
US4923532A (en) * 1988-09-12 1990-05-08 Allied-Signal Inc. Heat treatment for aluminum-lithium based metal matrix composites
US4933007A (en) * 1988-10-21 1990-06-12 Showa Aluminum Heat-resistant aluminum-base composites and process of making same
US5028301A (en) * 1989-01-09 1991-07-02 Townsend Douglas W Supersaturation plating of aluminum wettable cathode coatings during aluminum smelting in drained cathode cells
US5227045A (en) * 1989-01-09 1993-07-13 Townsend Douglas W Supersaturation coating of cathode substrate
US5039476A (en) * 1989-07-28 1991-08-13 Ube Industries, Ltd. Method for production of powder metallurgy alloy
US4917858A (en) * 1989-08-01 1990-04-17 The United States Of America As Represented By The Secretary Of The Air Force Method for producing titanium aluminide foil
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AU588990B2 (en) 1989-09-28
BR8701509A (pt) 1988-01-19
AU7093887A (en) 1987-10-08
JPH0583624B2 (ja) 1993-11-26
ES2025651T3 (es) 1992-04-01
EP0244949B1 (en) 1991-10-30
ATE69065T1 (de) 1991-11-15
JPS62238344A (ja) 1987-10-19
DE3774169D1 (de) 1991-12-05
EP0244949A1 (en) 1987-11-11

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